Perpendicular magnetic recording disk with template layer formed of nanoparticles embedded in a polymer material

ABSTRACT

A perpendicular magnetic recording disk includes a template layer below a Ru or Ru alloy underlayer, with a granular Co alloy recording layer formed on the underlayer. substrate. The template layer comprises nanoparticles spaced-apart and partially embedded within a polymer material, with the nanoparticles protruding above the surface of the polymer material. A seed layer covers the surface of the polymer material and the protruding nanoparticles and an underlayer of Ru or a Ru alloy covers the seed layer. The protruding nanoparticles serve as the controlled nucleation sites for the Ru or Ru alloy atoms. The nanoparticle-to-nanoparticle distances can be controlled during the formation of the template layer. This enables control of the Co alloy grain diameter distribution as well as grain-to-grain distance distribution.

RELATED APPLICATION

This application is related to concurrently-filed application ______titled “METHOD FOR MAKING A PERPENDICULAR MAGNETIC RECORDING DISK WITHTEMPLATE LAYER FORMED OF NANOPARTICLES EMBEDDED IN A POLYMER MATERIAL”(Attorney Docket No. HSJ920120115US1).

BACKGROUND OF THE INVENTION

1. Field of the Invention

This invention relates generally to perpendicular magnetic recordingmedia, such as perpendicular magnetic recording disks for use inmagnetic recording hard disk drives, and more particularly to acontinuous-media type of perpendicular magnetic recording disk with agranular cobalt-alloy recording layer having controlled grain size.

2. Description of the Related Art

In a “continuous-media” perpendicular magnetic recording disk, therecording layer is a continuous layer of granular cobalt-alloy magneticmaterial that becomes formed into concentric data tracks containing themagnetically recorded data bits when the write head writes on themagnetic material. Continuous-media disks, to which the presentinvention is directed, are to be distinguished from“bit-patterned-media” (BPM) disks, which have been proposed to increasedata density. In BPM disks, the magnetizable material on the disk ispatterned into small isolated data islands such that there is a singlemagnetic domain in each island or “bit”. The single magnetic domains canbe a single grain or consist of a few strongly coupled grains thatswitch magnetic states in concert as a single magnetic volume. This isin contrast to continuous-media disks wherein a single “bit” may havemultiple magnetic domains separated by domain walls.

FIG. 1 is a schematic of a cross-section of a prior art perpendicularmagnetic recording continuous-media disk. The disk includes a disksubstrate and an optional “soft” or relatively low-coercivitymagnetically permeable underlayer (SUL). The SUL serves as a flux returnpath for the field from the write pole to the return pole of therecording head. The material for the recording layer (RL) is a granularferromagnetic cobalt (Co) alloy, such as a CoPtCr alloy, with ahexagonal-close-packed (hcp) crystalline structure having the c-axisoriented substantially out-of-plane or perpendicular to the RL. Thegranular cobalt alloy RL should also have a well-isolated fine-grainstructure to produce a high-coercivity (H_(c)) media and to reduceintergranular exchange coupling, which is responsible for high intrinsicmedia noise. Enhancement of grain segregation in the cobalt alloy RL isachieved by the addition of oxides, including oxides of Si, Ta, Ti, Nb,B, C, and W. These oxides (Ox) tend to precipitate to the grainboundaries as shown in FIG. 1, and together with the elements of thecobalt alloy form nonmagnetic intergranular material. An optionalcapping layer (CP), such as a granular Co alloy without added oxides orwith smaller amounts of oxides than the RL, is typically deposited onthe RL to mediate the intergranular coupling of the grains of the RL,and a protective overcoat (OC) such as a layer of amorphous diamond-likecarbon is deposited on the CP.

The Co alloy RL has substantially out-of-plane or perpendicular magneticanisotropy as a result of the c-axis of its hexagonal-close-pack (hcp)crystalline structure being induced to grow substantially perpendicularto the plane of the layer during deposition. To induce this growth ofthe hcp RL, intermediate layers of ruthenium (Ru1 and Ru2) are locatedbelow the RL. Ruthenium (Ru) and certain Ru alloys, such as RuCr, arenonmagnetic hcp materials that induce the growth of the RL. An optionalseed layer (SL) may be formed on the SUL prior to deposition of Ru1.

The enhancement of segregation of the magnetic grains in the RL by theadditive oxides as segregants is important for achieving high arealdensity and recording performance. The intergranular Ox segregantmaterial not only decouples intergranular exchange but also exertscontrol on the size and distribution of the magnetic grains in the RL.Current disk fabrication methods achieve this segregated RL by growingthe RL on the Ru2 layer that exhibits columnar growth of the Ru orRu-alloy grains.

FIG. 2 is a transmission electron microscopy (TEM) image of a portion ofthe surface of a prior art CoPtCr—SiO₂ RL from a disk similar to thatshown in FIG. 1. FIG. 2 shows well-segregated CoPtCr magnetic grainsseparated by intergranular SiO₂ (white areas). However, as is apparentfrom FIG. 2, there is a relatively wide variation in the size of themagnetic grains and thus the grain-to-grain distance. A large grain sizedistribution is undesirable because it results in a variation inmagnetic recording properties across the disk and because some of thesmaller grains can be thermally unstable, resulting in loss of data.FIG. 2 also illustrates the randomness of grain locations. Because thenucleation sites during the sputtering deposition are randomlydistributed by nature, there is no control of the grain locations. Theamount of Ox segregants inside the RL needs to be sufficient to provideadequate grain-to-grain separation, but not too high to destroy thethermal stability of the RL. The typical content of the Ox segregants isabout 20% in volume, and the grain boundary thickness is typicallybetween about 1.0 and 1.5 nm.

To achieve high areal density of 1 to 5 Terabits/in² and beyond, it isdesirable to have high uniformity (or tighter distribution) of thegrains within the RL, mainly for the following three structuralparameters: grain diameter (i.e., the diameter of a circle that wouldhave the same area as the grain), grain-to-grain distance (i.e., thedistance between the centers of adjacent grains or “pitch”) and grainboundary thickness. Narrower distribution of these three structuralparameters will lead to narrower distributions of magnetic exchangeinteraction and magnetic anisotropy strength, both of which aredesirable.

Thus the prior art RL shown in FIG. 2 is far from ideal. First, thegrains have an irregular polygonal shape with a large size distribution.The average grain diameter is about 8-11 nm with a relatively large sizedistribution of about 18-22%. The distribution information is obtainedby measuring neighboring grain-to-grain distances in high resolutionscanning electron microscopy (SEM) or TEM images and then fitting with alognormal function. Distribution value as referred to in thisapplication shall mean the width of the lognormal function. Second, thelocation of the grain centers is highly random, which means there is noshort range or local ordering, i.e., no pattern within approximately 3-5grain distances. Third, the thickness of the grain boundaries (the Oxsegregants seen as white areas in FIG. 2) has an even widerdistribution. Typical grain boundary thickness is 0.9-1.2 nm with adistribution of about 50 to 70%. Because the intergranular exchange isan exponential decay function of boundary thickness, the largedistribution of boundary thickness leads to large fluctuation ofexchange between grains and thus a significant signal-to-ratio (SNR)loss. According to Wang et al, “Understanding Noise Mechanism in SmallGrain Size Perpendicular Thin Film Media”, IEEE Trans Mag 46, 2391(2010), a large distribution of boundary thickness can cause 3 to 10 dBSNR loss, and small-grain media suffer even more SNR loss thanlarge-grain media.

What is needed is a continuous-media perpendicular magnetic recordingdisk that has a granular cobalt alloy RL with additive oxides withwell-segregated magnetic grains with a narrow distribution of graindiameter and grain boundary thickness.

SUMMARY OF THE INVENTION

The invention relates to a continuous-media perpendicular magneticrecording disk with a granular Co alloy recording layer (RL) havingcontrolled grain size distribution and a method for making the disk withcontrolled location of nucleation sites.

The disk includes a substrate with a template layer formed on thesubstrate. The template layer comprises nanoparticles spaced-apart andpartially embedded within a polymer material having a functional endgroup. The nanoparticles protrude above the surface of the polymermaterial. A seed layer, like a NiTa alloy or an amorphous CoFeTaZralloy, covers the surface of the polymer material and the protrudingnanoparticles and an underlayer or Ru or a Ru alloy covers the seedlayer. A perpendicular magnetic RL comprising a layer of granularferromagnetic Co alloy and one or more oxides of one or more of Si, Ta,Ti Nb, B, C, and W is formed on the underlayer.

The seed layer generally replicates the surface topology of theunderlying template layer. The Ru or Ru alloy underlayer defines thetexture for the growth of the Co alloy RL. Because the nanoparticleswith protruding top surfaces serve as the controlled nucleation sites,the Ru or Ru alloy atoms preferentially nucleate on top of the small“bumps” created by the underlying protruding nanoparticles. The Rugrains are thus highly disconnected, which results in a monolayer of Ruor Ru alloy islands with an arrangement that generally replicates thearrangement of the underlying spaced-apart nanoparticles. The Co alloyhas a hexagonal-close-packed (hcp) crystalline structure having thec-axis oriented substantially out-of-plane or perpendicular to the RL.The Ru islands promote the growth of the Co alloy grains of the RL sothat the c-axis of the hcp Co alloy material is oriented substantiallyperpendicular, thereby resulting in perpendicular magnetic anisotropy.The oxide segregants generally form as intergranular material betweenthe Co alloy grains.

The nanoparticle-to-nanoparticle distances can be controlled during theformation of the template layer. This enables control of the Co alloygrain diameter distribution as well as grain-to-grain distancedistribution.

For a fuller understanding of the nature and advantages of the presentinvention, reference should be made to the following detaileddescription taken together with the accompanying figures.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic of a cross-section of a perpendicular magneticrecording disk according to the prior art.

FIG. 2 is a transmission electron microscopy (TEM) image of a portion ofa surface of a CoPtCr—SiO₂ recording layer of a prior art perpendicularmagnetic recording disk similar to the disk depicted in FIG. 1.

FIG. 3 is a side sectional view of the continuous-media perpendicularmagnetic recording disk according to this invention illustrating atemplate layer (TL) and at least one seed layer (SL1) located betweenthe substrate and the Ru or Ru alloy underlayer (UL).

FIG. 4A is a side sectional schematic showing a first step in the methodof forming the template layer (TL) in the disk according to theinvention.

FIG. 4B is a top schematic showing the generally hexagonal close packed(hcp) short range ordering of the nanoparticles of the TL depicted inFIG. 4A.

FIG. 4C is an SEM image showing a comparison of the array ofnanoparticles of the TL as spin-coated (left side of FIG. 4C) and aftersolvent annealing (right side of FIG. 4C), wherein the inset in eachfigure is the diffraction pattern generated by Fast FourierTransformation of the entire image.

FIG. 4D illustrates the step of etching away a portion of the polymermaterial of the film shown in FIG. 4A to expose the surfaces of thenanoparticles of the TL.

FIG. 4E illustrates the step of homogenizing the surface of the TLdepicted in FIG. 4D.

FIG. 4F illustrates the step of depositing the remaining layers of thedisk according to the invention.

FIG. 5 is an Electron Energy Loss Spectroscopy-Scanning TransmissionElectron Microscopy (EELS-STEM) composite image of a 2.3 nm Ru layerformed by templated growth on top of a template layer (TL) according tothe invention.

FIG. 6 is a TEM image of a portion of a surface of a CoPtCr—SiO₂recording layer of a perpendicular magnetic recording disk according tothe invention.

DETAILED DESCRIPTION OF THE INVENTION

FIG. 3 is a side sectional view of the continuous-media perpendicularmagnetic recording disk according to the invention. In the diskaccording to this invention a template layer (TL) and at least one seedlayer (SL1), both of which will be described in detail below, arelocated between the substrate and the Ru or Ru alloy underlayer (UL).

The disk substrate may be any commercially available glass substrate ora wafer or disk of a material such as, but not limited to, silicon (Si),fused quartz, carbon, or a silicon nitride (SiN_(x)). An optionalconventional SUL (not shown in FIG. 3) may be located between thesubstrate and the TL. The SUL may be a single soft magnetic layer (asshown in FIG. 1) or a multilayer of soft magnetic layers separated bynonmagnetic layers. The SUL layer or layers are formed of amorphousmagnetically permeable materials such as alloys of CoNiFe, FeCoB,CoCuFe, NiFe, FeAlSi, FeTaN, FeN, FeTaC, CoTaZr, CoFeB, and CoZrNb. Thethickness of the SUL is typically in the range of approximately 20-400nm.

An optional second seed layer (SL2) may be formed on SL1 and anunderlayer (UL) of ruthenium (Ru) or a Ru alloy is formed on SL2, or SL1if there is no SL2. The Ru or Ru alloy UL is formed as disconnectedislands 30 over the SL2, or the SL1 if there is no SL2. The recordinglayer (RL) is a granular ferromagnetic cobalt (Co) alloy, such as aCoPtCr alloy or a CoPtCrB alloy, with intergranular oxides, includingoxides of one or more of Si, Ta, Ti, Nb, B, C, and W. The Co alloy has ahexagonal-close-packed (hcp) crystalline structure having the c-axisoriented substantially out-of-plane or perpendicular to the RL. The Ruislands 30 of the UL promote the growth of the Co alloy grains 40 of theRL so that the c-axis of the hcp Co alloy material is orientedsubstantially perpendicular, thereby resulting in perpendicular magneticanisotropy. The oxide segregants generally form as intergranularmaterial 45 between the Co alloy grains 40.

An optional conventional capping layer (CP), such as a granular Co alloywithout added oxides or with smaller amounts of oxides than the RL, istypically deposited on the RL to mediate the intergranular coupling ofthe grains of the RL. A conventional protective overcoat (OC) such as alayer of amorphous diamond-like carbon is typically deposited on the CP,or on the RL if there is no CP.

The TL comprises nanoparticles 10 spaced-apart by and embedded within amatrix of polymer material 20. As shown in FIG. 3, the nanoparticleshave upper surfaces not covered by the polymer material that are exposedprior to deposition of SL1.

Nanoparticles (also called nanocrystals) include small sub-100 nm sizedcrystalline particles composed of materials such as CdSe, CdTe, PbSe,FePt, iron oxide (FeOx), Si, ZnO, Au, Ru, Cu, Ag, and vanadium oxide(VO_(x)). Nanoparticles can be synthesized in a variety of sizes andwith narrow size distributions. For example, CdSe nanoparticles arecommercially available with diameters ranging from 2-7 nm. Othersemiconductor nanoparticles are also available. This includes III-Vsemiconductors as described in D. V. Talapin, MRS Bulletin 37, 63-71(2012) and in Green, “Solution routes to III-V semiconductor quantumdots”, Current Opinion in Solid State and Materials Science 6, pp.355-363 (2002).

The invention will be described for an example where the nanoparticlesare iron-oxide (Fe₃O₄), and the polymer material is polystyrene with anend group of COOH. FIG. 4A is a side sectional schematic showing a firststep in the method of forming the TL. A film comprising Fe₃O₄nanoparticles 10 embedded in the polymer material 20 is formed on thesubstrate surface. The nanoparticles 10 are separated by the attachedpolystyrene chains 12. As depicted in FIG. 4A and the top schematic ofFIG. 4B, the nanoparticles 10 have short range ordering withinapproximately 3-5 grain distances, which means that within this shortrange they are arranged in a generally uniform pattern on the substratesurface. The film is formed by spin coating a solution of thenanoparticles and polymer material on the substrate surface and allowingthe solution dry, although other methods of dispersal are possible.Fe₃O₄ nanocrystals with a diameter of between about 1-10 nm and havingpolystyrene ligands with molecular weight between about 0.3-10 kg/molare dissolved in toluene (or other solvent) at a concentration of about1-25 mg/ml. A single layer of Fe₃O₄ nanoparticles can be formed acrossthe substrate surface with relatively high uniformity by properselection of the concentration of nanoparticles in the toluene solutionand the spinning speed. During this process, the ligand molecules formcross-links to construct a continuous film of polystyrene, within whichthe Fe₃O₄ nanoparticles are embedded. The process for forming the filmof Fe₃O₄ nanoparticles embedded in the matrix of polymer material toform a single layer of generally uniformly distributed Fe₃O₄nanoparticles is described by Fischer et al., “Completely MiscibleNanocomposites”, Angew. Chem. Int. Ed. 2011, 50, 7811-7814.

As an optional step, after the solution has been applied to thesubstrate surface the substrate may be solvent annealed or thermallyannealed, or both, for example by exposing the spin-coated film to atoluene (or other solvent) vapor or by thermally annealing at 250° C.,to facilitate organization of the nanoparticles into the generally moreuniform pattern. The optional solvent annealing step adjusts theordering of the array of nanoparticles. Solvent annealing is performedin an enclosed chamber filled with toluene vapor for a certain period oftime, for example 30 minutes. During the solvent annealing process,toluene vapor penetrates the polystyrene matrix and causes swelling ofthe film. When the polystyrene swells, the Fe₃O₄ nanoparticles are ableto move around and re-assemble to form a more uniform or closer packedpattern. FIG. 4C shows a comparison of the array of Fe₃O₄ nanoparticlesas spin-coated (left side of FIG. 4 C) and after solvent annealing for30 minutes (right side of FIG. 4C), and illustrates the improvement inordering, particularly the short range ordering, as a result of thesolvent annealing. The distribution of particle-to-particle distance canbe controlled by the solvent annealing step. For example, as-spunparticles normally have a distribution around 10-15%, and particlessolvent annealed for 30 minutes have a distribution around 5-10%.Solvent annealing for an even longer time would achieve an even smallerdistribution.

FIG. 4D illustrates the step of etching away a portion of the polymermaterial 20 of the film shown in FIG. 4A to expose the surfaces of theFe₃O₄ nanoparticles 10. This results in the Fe₃O₄ nanoparticles 10 beingonly partially embedded in the matrix of polymer material 20. An oxygen(O₂) plasma reacts with the polystyrene chains and turns them into gasand water vapor, which are pumped away. Because the nanoparticles are anoxide they are not significantly affected by the O₂ plasma. Bycontrolling the plasma treating time and the plasma intensity, theamount of polystyrene stripped away can be controlled, and thus theamount of protrusion of the Fe₃O₄ nanoparticles can be controlled. Thepreferred amount of protrusion of the Fe₃O₄ nanoparticles is betweenabout 35 to 75 percent of the diameter of the nanoparticles. This isaccomplished with a O₂ plasma treatment for about 30-50 seconds. Afterthe partial removal of the polystyrene, the surface has topographicprotrusions of Fe₃O₄ nanoparticles 10, as well as a chemical contrastbetween the Fe₃O₄ nanoparticle 10 surfaces and the surrounding remainingpolystyrene material 20. While etching of sufficient polymer material toexpose the surfaces of the nanoparticles is preferred because it resultsin both a topographic surface and a chemical contrast, the polymermaterial may be etched to a lesser extent so that the nanoparticles maystill retain a thin film of polymer material but still produce atopographic surface.

FIG. 4E illustrates the step of homogenizing the surface of FIG. 4D. Athin amorphous metallic layer serves as a first seed layer (SL1). SL1 ispreferably a NiTa alloy or a CoFeTaZr alloy, sputter deposited onto theexposed surfaces of the Fe₃O₄ nanoparticles 10 and the surface of theremaining polystyrene material 20 to a thickness between about 1 to 5nm. The SL1 thus conforms to and generally replicates the topographicsurface of the exposed nanoparticles 10 and surrounding polymer material20. At this thickness, SL1 is adequate to cover the entire surface, butnot too thick to wash out the protrusion features of the nanoparticles10. After this step, the TL with SL1 is complete and ready for templatedgrowth of the RL.

FIG. 4F illustrates the steps of depositing the remaining layers of thedisk according to the invention. An optional second seed layer (SL2) issputter deposited onto SL1. SL2 is a seed layer for the growth of the Ruor Ru alloy UL. SL2 is preferably a highly crystalline material, like aNiW alloy, with a thickness between about 3 to 10 nm, but SL2 may alsobe formed of NiV or NiFeW alloys. The SL2 improves the crystallinity ofthe hcp Ru or Ru alloy UL. Next a Ru layer is sputter deposited as theUL to a thickness between about 5 to 15 nm. The Ru UL defines the (0001)texture for the growth of the Co alloy RL. Due to the surface topologyof the underlying SL1 and optional SL2, the Ru atoms preferentiallynucleate on top of the small “bumps” created by the underlying Fe₃O₄nanoparticles 10. The Ru grains are thus highly disconnected. Thisresults in a monolayer of Ru islands 30 with an arrangement thatreplicates the arrangement of the underlying Fe₃O₄ nanoparticles 10. Thepressure of Ar gas is an important factor during the sputtering of Rubecause it determines the roughness of the Ru surface. Low Ar pressure(1-10 mTorr) leads to a rather smooth Ru surface and high Ar pressure(10-50 mTorr) leads to higher roughness. The fine control of Ruroughness by Ar pressure can be used to tune the extent of segregationamong the RL grains which are grown on top of the Ru surface. Higherroughness in Ru causes stronger separation among the magnetic grains andless magnetic exchange coupling. In this invention, the Ar pressure ispreferably between about 10 to 50 mTorr. While Ru is a commonly usedmaterial for the UL, the UL may also be formed of Ru-based alloys suchas a RuCr alloy.

FIG. 5 is an EELS-STEM composite image of a 2.3 nm Ru layer formed bytemplated growth on top of a TL according to the invention. The TL wasFe₃O₄ nanoparticles partially embedded in polystyrene material with aSL1 formed of a NiTa alloy. The circular grains are formed by Ru, andthe white dot in the center of each grain is the location of the Fe₃O₄nanoparticle, obtained from the Fe-signal in EELS. The white dot withineach island show the mapping of the underlying Fe element, proving thatthe Ru islands are formed on top of the Fe₃O₄ nanoparticles. FIG. 5 alsoillustrates that the Ru islands have short range ordering, i.e., theyform a generally uniform pattern within approximately 3-5 islanddistances.

Next the RL of a conventional Co alloy and one or more oxides is sputterdeposited onto the Ru or Ru alloy UL. The RL is a granular ferromagneticcobalt (Co) alloy, such as a CoPtCr alloy or a CoPtCrB alloy, withintergranular oxides, including oxides of one or more of Si, Ta, Ti, andNb. The Co alloy has a hexagonal-close-packed (hcp) crystallinestructure having the c-axis oriented substantially out-of-plane orperpendicular to the RL. The Ru islands 30 promote the growth of the Coalloy grains 40 of the RL so that the c-axis of the hcp Co alloymaterial is oriented substantially perpendicular, thereby resulting inperpendicular magnetic anisotropy. The oxide segregants generally formas intergranular material 45 between the Co alloy grains 40.

To complete the disk shown in FIG. 4F, an optional capping layer (CP)may be deposited on the RL, followed by the disk protective overcoat(OC). The CP typically consists of a ferromagnetic granular Co alloy,like a CoPtCr or CoPtCrB alloy, for mediating or controlling theintergranular exchange coupling in the RL. Thus the CP may have agreater amount of Cr and/or B than the RL, or a lesser amount of oxidesthan the RL. For example, the CP may have substantially the same Coalloy composition as the RL but have no oxides. As a result, theindividual Co alloy grains of the CP are larger than the Co alloy grainsof the RL and generally overlap multiple grains of the RL. The OC formedon the CP, or on the RL if there is no CP, may be an amorphousdiamond-like carbon film or other known protective overcoat, such assilicon nitride (SiN).

FIG. 6 is a TEM image of a portion of a surface of a CoPtCr—SiO₂recording layer of a perpendicular magnetic recording disk according tothe invention. FIG. 6 shows that the Co alloy grains have a generallyhexagonal shape, as compared with the generally irregular shape of thegrains in FIG. 2. More importantly, by comparison with the prior art ofFIG. 2, in FIG. 6 the distribution of grain diameter is only about 8%and the boundary thickness is also more uniform. This smaller value ofgrain diameter distribution can be accomplished by the optional step ofannealing, e.g., solvent annealing, as described above. While theinvention can accomplish this very narrow distribution of 8% for thegrain diameters, it has been found as part of this invention that thisrelatively low value can cause “synchronizing noise”, i.e. noise withuniform peaks. Thus it may be desirable for continuous perpendicularmagnetic recording media that the distribution of grain diameters bewithin about 10-15%. This can be accomplished by not performing theannealing step, so that the nanoparticles have the arrangement show inon the left side in FIG. 4C, or by reducing the length of time for theoptional solvent annealing step.

The template layer (TL) for the disk of this invention has beendescribed for Fe₃O₄ nanoparticles partially embedded in a polymermaterial of polystyrene with a functional end group of COOH. However,examples of other nanoparticles include, but are not limited to,zinc-oxide (ZnO), silver (Ag), gold (Au), cadmium selenide (CdSe),cobalt (Co), iron-platinum (FePt), copper (Cu), and vanadium oxide (VOx)(e.g., VO₂, V₂O₃, V₂O₅). Examples of other polymers include, but are notlimited to, polydimethyl siloxane, polysiloxane, polyisoprene,polybutadiene, polyisobutylene polypropylene glycol, and polyethyleneglycol. Examples of other functional end groups for the polymersinclude, but are not limited to, carbocyl group (COOH), hydroxyl group(OH), amino group (NH(CH₂)₂NH₂) and thiol group (CSH).

While the present invention has been particularly shown and describedwith reference to the preferred embodiments, it will be understood bythose skilled in the art that various changes in form and detail may bemade without departing from the spirit and scope of the invention.Accordingly, the disclosed invention is to be considered merely asillustrative and limited in scope only as specified in the appendedclaims.

What is claimed is:
 1. A perpendicular magnetic recording diskcomprising: a substrate; a template layer on the substrate, the templatelayer comprising nanoparticles spaced-apart by and embedded within apolymer material, the nanoparticles providing protrusion features at thesurface of the polymer material; a seed layer covering the polymermaterial and the nanoparticles; an underlayer selected from Ru and a Rualloy on the seed layer; and a perpendicular magnetic recording layer onthe underlayer and comprising a layer of granular ferromagnetic Co alloyand one or more oxides of one or more of Si, Ta, Ti Nb, B, C, and W. 2.The disk of claim 1 wherein the nanoparticles are Fe₃O₄ nanoparticlesand the polymer material comprises polystyrene having a functional endgroup.
 3. The disk of claim 1 wherein the seed layer is selected from anamorphous NiTa alloy and an amorphous CoFeTaZr alloy.
 4. The disk ofclaim 1 wherein the seed layer has a thickness greater than or equal to1 nm and less than or equal to 5 nm.
 5. The disk of claim 1 wherein theseed layer is a first seed layer and further comprising a second seedlayer on and in contact with the first seed layer, and wherein theunderlayer is on and in contact with the second seed layer.
 6. The diskof claim 5 wherein the first seed layer comprises a NiTa alloy and thesecond seed layer comprises a NiW alloy.
 7. The disk of claim 1 whereinthe nanoparticles are partially embedded within the polymer material,whereby the nanoparticles protrude above the surface of the polymermaterial and have surfaces not covered by the polymer material.
 8. Thedisk of claim 7 wherein between 35 to 75 percent of the diameter of thenanoparticles is above the surface of the polymer material.
 9. The diskof claim 1 wherein the nanoparticles are arranged in a generally uniformpattern with short range ordering.
 10. The disk of claim 1 wherein thedistribution of nanoparticle-to-nanoparticle distance is greater than orequal to 5% and less than or equal to 10%.
 11. The disk of claim 1wherein the distribution of nanoparticle-to-nanoparticle distance isgreater than or equal to 10% and less than or equal to 15%.
 12. The diskof claim 1 wherein the granular ferromagnetic Co alloy comprises grainshaving a grain diameter distribution of greater than or equal to 10% andless than or equal to 15%.
 13. The disk of claim 1 further comprising asoft magnetically permeable underlayer (SUL) between the substrate andthe template layer.
 14. A perpendicular magnetic recording diskcomprising: a substrate; a template layer on the substrate, the templatelayer comprising Fe₃O₄ nanoparticles spaced-apart by and partiallyembedded within a polymer material comprising polystyrene having afunctional end group, the nanoparticles protruding above the surface ofthe polymer material and having surfaces not covered by the polymermaterial; a seed layer selected from an amorphous NiTa alloy and anamorphous CoFeTaZr alloy covering the surface of the polymer materialand the surfaces of the nanoparticles; an underlayer selected from Ruand a Ru alloy on the seed layer; and a perpendicular magnetic recordinglayer on the underlayer and comprising a layer of granular ferromagneticCo alloy and one or more oxides of one or more of Si, Ta, Ti Nb, B, C,and W.
 15. The disk of claim 14 wherein the seed layer has a thicknessgreater than or equal to 1 nm and less than or equal to 5 nm.
 16. Thedisk of claim 14 wherein the seed layer is a first seed layer andfurther comprising a second seed layer on and in contact with the firstseed layer, and wherein the underlayer is on and in contact with thesecond seed layer.
 17. The disk of claim 16 wherein the first seed layercomprises a NiTa alloy and the second seed layer comprises a NiW alloy.18. The disk of claim 14 wherein between 35 to 75 percent of thediameter of the nanoparticles is above the surface of the polymermaterial.
 19. The disk of claim 14 wherein the nanoparticles arearranged in a generally uniform pattern with short range ordering. 20.The disk of claim 14 wherein the distribution ofnanoparticle-to-nanoparticle distance is greater than or equal to 5% andless than or equal to 10%.
 21. The disk of claim 14 wherein thedistribution of nanoparticle-to-nanoparticle distance is greater than orequal to 10% and less than or equal to 15%.
 22. The disk of claim 14wherein the granular ferromagnetic Co alloy comprises grains having agrain diameter distribution of greater than or equal to 10% and lessthan or equal to 15%.
 23. The disk of claim 14 further comprising a softmagnetically permeable underlayer (SUL) between the substrate and thetemplate layer.